Bioresorbable scaffold for treatment of bifurcation lesion

ABSTRACT

Bioresorbable scaffolds for treatment of bifurcation lesion are described herein. Generally, an expandable scaffold may be fabricated from a high molecular weight isotropic PLLA material, wherein the scaffold incorporates one or more strain relief features which are configured to allow side branch treatment.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation of U.S. patent application Ser. No. 14/334,562 filed Jul. 17, 2014, which claims the benefit of priority to U.S. Prov. App. 61/866,859 filed Aug. 16, 2013, each of which is incorporated herein by reference in its entirety.

FIELD OF THE INVENTION

The present invention relates generally to stent or scaffold delivery and deployment methods and apparatus. More particularly, the present invention relates to methods and apparatus for bioresorbable scaffolds which may be used for the treatment of bifurcation lesions.

BACKGROUND OF THE INVENTION

In treating diseased vessels, particularly blood vessels which have one or more side branches extending from a main vessel, difficulties may arise when implanting stents at these junctions to treat lesions. For instance, when implanting a stent along the main vessel, the openings to the side branches may become restricted by the stent walls. Although open cells along the stents may be expanded in size to allow for greater flow between the main vessel and side branch, such enlarging of the open cells may present additional challenges.

For instance, enlarging the open cell may create a number of cracks or failures in the stent struts. This may be the case particularly when attempting to enlarge an open cell in a bioresorbable polymeric stent or scaffold.

Because many polymeric implants such as stents are fabricated through processes such as extrusion or injection molding, such methods typically begin the process by starting with an inherently weak and brittle material. In the example of a polymeric stent, the resulting stent may be susceptible to brittle fracture especially upon expansion. Also, as described above, due to their inherent weakness and embrittlement, a selective enlargement of the cell is not possible with these stents without causing mechanical failure in their structure.

A stent which is susceptible to brittle fracture is generally undesirable because of its limited ability to collapse for intravascular delivery as well as its limited ability to expand for placement or positioning within a vessel. Moreover, such polymeric stents also exhibit a reduced level of strength. Brittle fracture is particularly problematic in stents as placement of a stent onto a delivery balloon or within a delivery sheath imparts a substantial amount of compressive force in the material comprising the stent. A stent made of a brittle material may crack or have a very limited ability to collapse or expand without failure. Thus, a certain degree of malleability is desirable for a stent to expand, deform, and maintain its position securely within the vessel.

Accordingly, it is desirable to produce a polymeric substrate having one or more layers which retains its mechanical strength and is sufficiently ductile so as to prevent or inhibit brittle fracture, particularly when utilized as a biocompatible and/or bioabsorbable polymeric stent for implantation within a patient body. Additionally, it is desirable to produce a polymeric stent which can be deployed and expanded within a vessel lumen and then have one or more open cells defined along the stent further enlarged without cracking or failure of the struts.

SUMMARY OF THE INVENTION

A blood vessel often has numerous side-branches that vascularize tissues that are relatively far from the main vessel. When the vessels develop a disease, e.g., arteriosclerosis that obstructs the flow within the main vessel, side branch, or both, the obstruction may occur at the junction of the main vessel and one of its side branches. If flow patency in both the main vessel and the side branch is desired, one can deploy a stent in the main vessel at the junction where the side branch extends and then treat the side branch with balloon angioplasty or by stenting. However, the stent that has been placed in the main vessel may obstruct part of the opening to the side branch and cause flow reduction or other negative effects.

In order to reduce the side branch flow obstruction, a practitioner can expand the junction between the main vessel and the side branch, e.g., with an angioplasty balloon or with a stent. Doing so may require a balloon catheter or a stent to be tracked within the main vessel, into the expanded stent, and then through an open cell defined along the main vessel stent adjacent to the opening of the side branch. Once the catheter has been advanced along pathway, an inflatable balloon (or other expansion mechanism) located along the catheter, may be positioned within an expanded open cell which is located at or in proximity to the opening of the side branch Where a periphery of the open cell is defined by adjacent circumferential rings and longitudinal struts framing the open cell. The inflatable balloon may then be expanded to enlarge the open cell to a further enlarged configuration without disrupting or reconfiguring the remainder of the stent to provide a more open flow path through the opening to the side branch. However, enlarging the open cells of an already expanded stent may form or create cracks in the stent struts leading to failure for metallic stents and particularly for bioresorbable polymeric stents.

With respect to the bioresorbable polymer itself, a number of casting processes described herein may be utilized to develop substrates, e.g., cylindrically shaped substrates, having a relatively high level of geometric precision and mechanical strength. These polymeric substrates can then be machined using any number of processes (e.g., high-speed laser sources, mechanical machining, etc.) to create devices such as stents having a variety of geometries for implantation within a patient, such as the peripheral or coronary vasculature, etc.

An example of such a casting process is to utilize a dip-coating process. The utilization of dip-coating to create a polymeric substrate having such desirable characteristics results in substrates which are able to retain the inherent properties of the starting materials. This in turn results in substrates having a relatively high radial strength which is retained through any additional manufacturing processes for implantation. Additionally, dip-coating the polymeric substrate also allows for the creation of substrates having multiple layers.

The molecular weight of a polymer is typically one of the factors in determining the mechanical behavior of the polymer. With an increase in the molecular weight of a polymer, there is generally a transition from brittle to ductile failure. A mandrel may be utilized to cast or dip-coat the polymeric substrate.

In dip-coating the polymeric substrate, one or more high molecular weight biocompatible and for bioabsorbable polymers may be selected for forming upon the mandrel. The one or more polymers may be dissolved in a compatible solvent in one or more corresponding containers such that the appropriate solution may he placed under the mandrel. As the substrate may be formed to have one or more layers overlaid upon one another, the substrate may be formed to have a first layer of a first polymer, a second layer of a second polymer, and so on depending upon the desired structure and properties of the substrate. Thus, the various solutions and containers may be replaced beneath the mandrel between dip-coating operations in accordance with the desired layers to be formed upon the substrate such that the mandrel may be dipped sequentially into the appropriate polymeric solution.

Parameters such as the number of times the mandrel is immersed, the sequence and direction of dipping, the duration of time of each immersion within the solution, as well as the delay time between each immersion or the drying or curing time between dips and dipping and/or withdrawal rates of the mandrel to and/or from the solution may each be controlled to result in the desired mechanical characteristics. Formation via the dip-coating process may result in a polymeric substrate having half the wall thickness while retaining an increased level of strength in the substrate as compared to an extruded polymeric structure.

The immersion times as well as drying times may be uniform between each immersion or they may be varied as determined by the desired properties of the resulting substrate. Moreover, the substrate may be placed in an oven or dried at ambient temperature between each immersion or after the final immersion to attain a predetermined level of crystals, e.g., 60%, and a level of amorphous polymeric structure, e.g., 40%. Each of the layers overlaid upon one another during the dip-coating process are tightly adhered to one another and the wall thicknesses and mechanical properties of each polymer are retained in their respective layer with no limitation on the molecular weight and/or crystalline structure of the polymers utilized.

Dip-coating can be used to impart an orientation between layers (e.g., linear orientation by dipping; radial orientation by spinning the mandrel; etc.) to further enhance the mechanical properties of the formed substrate. As radial strength is a desirable attribute of stent design, post-processing of the forged substrate may be accomplished to impart such attributes. Typically, polymeric stents suffer from having relatively thick walls to compensate for the lack of radial strength, and this in turn reduces flexibility, impedes navigation, and reduces arterial luminal area immediately post implantation. Post-processing may also help to prevent material creep and recoil (creep is a time-dependent permanent deformation that occurs to a specimen under stress, typically under elevated temperatures) which are problems typically associated with polymeric stents.

For post-processing, a predetermined amount of force may be applied to the substrate where such a force may be generated by a number of different methods. One method is by utilizing an expandable pressure vessel placed within the substrate. Another method is by utilizing a braid structure, such as a braid made from a super-elastic or shape memory alloy like NiTi alloy, to increase in size and to apply the desirable degree of force against the interior surface of the substrate.

Yet another method may apply the expansion force by application of a pressurized inert gas such as nitrogen within the substrate lumen. A completed substrate may be placed inside a molding tube which has an inner diameter that is larger than the cast cylinder. A distal end or distal portion of the cast cylinder may be clamped or otherwise closed and a pressure source may be coupled to a proximal end of the cast cylinder. The entire assembly may be positioned over a nozzle which applies heat to either the length of the cast cylinder or to a portion of cast cylinder. The increase in diameter of the cast cylinder may thus realign the molecular orientation of the cast cylinder to increase its radial strength. After the diameter has been increased, the cast cylinder may be cooled.

Once the processing has been completed on the polymeric substrate, the substrate may be further formed or machined to create a variety of device. One example includes stents created from the cast cylinder by cutting along a length of the cylinder to create a rolled stent for delivery and deployment within the patient vasculature. Another example includes machining a number of portions to create a lattice or scaffold structure which facilitates the compression and expansion of the stent.

In other variations, in forming the stent, the substrate may be first formed at a first diameter, as described herein by immersing a mandrel into at least a first polymeric solution such that at least a first layer of a biocompatible polymer substrate is formed upon the mandrel and has a first diameter defined by the mandrel. In forming the substrate, parameters such as controlling a number of immersions of the mandrel into the first polymeric solution, controlling a duration of time of each immersion of the mandrel, and controlling a delay time between each immersion of the mandrel are controlled. With the substrate initially formed, the first diameter of the substrate may be reduced to a second smaller diameter and processed to form an expandable stent scaffold configured for delivery and deployment within a vessel, wherein the stent scaffold retains one or more mechanical properties of the polymer resin such that the stent scaffold exhibits ductility upon application of a load.

With the stent scaffold formed and heat set to have an initial diameter, it may be reduced to a second delivery diameter and placed upon a delivery catheter for intravascular delivery within a patient body comprising positioning the stent having the second diameter at a target location within the vessel, expanding the stent to a third diameter that is larger than the second diameter (and possibly smaller than the initial diameter) at the target location utilizing an inflation balloon or other mechanism, and allowing the stent to then self-expand into further contact with the vessel at the target location such that the stent self-expands over time back to its initial diameter or until it is constrained from further expansion by the vessel walls.

Taking this bioresorbable stent, one method of increasing flow through a wall of a stent may comprise expanding the stent which defines a lumen therethrough from a delivery configuration into a deployed configuration, introducing an expansion device into the lumen and through an open cell defined along the wall of the stent, and enlarging the open cell from a first expanded configuration into a second enlarged configuration, wherein the stent is comprised of a bioresorbable polymer characterized by a molecular weight from 259,000 g/mol to 2,120,000 g/mol and a crystallinity from 20% to 40%.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 illustrates a stress-strain plot of polylactic acid (PLLA) at differing molecular weights and their corresponding stress-strain values indicating brittle fracture to ductile failure.

FIG. 2A illustrates an example of a dip-coating machine which may be utilized to form a polymeric substrate having one or more layers formed along a mandrel.

FIGS. 2B and 2C illustrate another example of a dip-coating assembly having one or more articulatable linkages to adjust a dipping direction of the mandrel.

FIGS. 3A to 3C show respective partial cross-sectional side and end views of an example of a portion of a multi-layer polymeric substrate formed along the mandrel and the resulting substrate.

FIG. 4A illustrates an example of a resulting stress-strain plot of various samples of polymeric substrates formed by a dip-coating process and the resulting plots indicating ductile failure.

FIG. 4B illustrates another example of a stress-strain plot of additional samples formed by dip-coating along with samples incorporating a layer of BaSO₄.

FIG. 4C illustrates an example of a detailed end view of a PLLA 8.28 substrate having a BaSO₄ layer incorporated into the substrate.

FIGS. 5A and 5B illustrate perspective views of an example of a dip-coat formed polymeric substrate undergoing plastic deformation and the resulting high percentage elongation.

FIG. 6 illustrates an example of an additional forming procedure where a formed polymeric substrate may be expanded within a molding or forming tube to impart a circumferential orientation into the substrate.

FIG. 7 illustrates another example of an additional forming procedure where a formed polymeric substrate may be rotated to induce a circumferentially-oriented stress value to increase the radial strength of the substrate.

FIG. 8 illustrates a perspective view of one example of a rolled sheet stent which may be formed with the formed polymeric substrate.

FIG. 9 illustrates a side view of another example of a stent machined via any number of processes from the resulting polymeric substrate.

FIGS. 10A to 10F illustrate side views of another example of how a stent formed from a polymeric substrate may be delivered and deployed initially via balloon expansion within a vessel and then allowed to self-expand further in diameter to its initial heat set diameter.

FIG. 11A shows a blood vessel having at least one side branch.

FIG. 11B shows a vessel which has developed obstructions at the junction of the main vessel and one of its side branches.

FIG. 12 shows a bioabsorbable stent placed in the main vessel obstructing the side branch.

FIGS. 13A and 13B show an example of how a balloon or a stent may be tracked through the main vessel into an open cell of the main vessel bioabsorbable stent and into the side branch.

FIGS. 14A and 14B show an example of how an open cell of the main vessel bioabsorbable stent may be enlarged to facilitate access into the side branch vessel.

FIGS. 15A and 15B show top views of an example of a bioabsorbable stent prior to and after an open cell is enlarged.

FIG. 16 shows an example of stent starts designed to incorporate strain relief features that can deform to distribute strain when an open cell is enlarged.

DETAILED DESCRIPTION OF THE INVENTION

In manufacturing implantable devices from polymeric materials such as biocompatible and/or biodegradable polymers, a number of casting processes described herein may be utilized to develop substrates, e.g. cylindrically shaped substrates, having a relatively high level of geometric precision and mechanical strength. These polymeric substrates can then be machined using any number of processes (e.g., high-speed laser sources, mechanical machining, etc.) to create devices such as stents having a variety of geometries for implantation within a patient, such as the peripheral or coronary vasculature, etc.

An example of such a casting process is to utilize a dip-coating process. The utilization of dip-coating to create a polymeric substrate having such desirable characteristics results in substrates which are able to retain the inherent properties of the starting materials. This in turn results in substrates having a relatively high radial strength which is mostly retained through any additional manufacturing processes for implantation. Additionally, dip-coating the polymeric substrate also allows for the creation of substrates having multiple layers. The multiple layers may be formed from the same or similar materials or they may be varied to include any number of additional agents, such as one or more drugs for treatment of the vessel, as described in further detail below. Moreover, the variability of utilizing multiple layers for the substrate may allow one to control other parameters, conditions, or ranges between individual layers such as varying the degradation rate between layers while maintaining the intrinsic molecular weight and mechanical strength of the polymer at a high level with minimal degradation of the starting materials.

Because of the retention of molecular weight and mechanical strength of the starting materials via the casting or dip-coating process, polymeric substrates may be formed which enable the fabrication of devices such as steins with reduced wall thickness which is highly desirable for the treatment of arterial diseases. Furthermore these processes may produce structures having precise geometric tolerances with respect to wall thicknesses, concentricity, diameter, etc.

One mechanical property in particular which is generally problematic with, e.g., polymeric stents formed from polymeric substrates, is failure via brittle fracture of the device when placed under stress within the patient body. It is generally desirable for polymeric stents to exhibit ductile failure under an applied load rather via brittle failure, especially during delivery and deployment of a polymeric stent from an inflation balloon or constraining sheath, as mentioned above. Percent (%) ductility is generally a measure of the degree of plastic deformation that has been sustained by the material at fracture. A material that experiences very little or no plastic deformation upon fracture is brittle.

The molecular weight of a polymer is typically one of the factors in determining the mechanical behavior of the polymer. With an increase in the molecular weight of a polymer, there is generally a transition from brittle to ductile failure. An example is illustrated in the stress-strain plot 10 which illustrate the differing mechanical behavior resulting from an increase in molecular weight. The stress-strain curve 12 of a sample of polylactic acid (PLLA) 2.4 shows a failure point 18 having a relatively low tensile strain percentage at a high tensile stress level indicating brittle failure. A sample of PLLA 4.3, which has a relatively higher molecular weight than PLLA 2.4, illustrates a stress-strain curve 14 which has a region of plastic failure 20 after the onset of yielding and a failure point 22 which has a relatively lower tensile stress value at a relatively higher tensile strain percentage indicating a degree of ductility. Yield occurs when a material initially departs from the linearity of a stress-strain curve and experiences an elastic-plastic transition.

A sample of PLLA 8.4, which has yet a higher molecular weight than PLLA 4.3, illustrates a stress-strain curve 16 which has a longer region of plastic failure 24 after the onset of yielding. The failure point 26 also has a relatively lower tensile stress value at a relatively higher tensile strain percentage indicating a degree of ductility. Thus, a high-strength tubular material which exhibits a relatively high degree of ductility may be fabricated utilizing polymers having a relatively high molecular weight (e.g., PLLA 8.4, PLLA with 8.28 IV, etc.). Such a tubular material may be processed via any number of machining processes to form an implantable device such as a stent which exhibits a stress-strain curve which is associated with the casting or dip-coating process described herein.

An example of a mandrel which may be utilized to cast or dip-coat the polymeric substrate is illustrated in the side view of FIG. 2A. Generally, dip coating assembly 30 may be any structure which supports the manufacture of the polymeric substrate in accordance with the description herein. A base 32 may support a column 34 which houses a drive column 36 and a bracket arm 38. Motor 42 may urge drive column 36 vertically along column 34 to move bracket arm 38 accordingly. Mandrel 40 may be attached to bracket arm 38 above container 44 which may be filled with a polymeric solution 46 (e.g., PLLA, PLA, PLGA, etc.) into which mandrel 40 may be dipped via a linear motion 52. The one or more polymers may be dissolved in a compatible solvent in one or more corresponding containers 44 such that the appropriate solution may be placed under mandrel 40. An optional motor 48 may be mounted along bracket arm 38 or elsewhere along assembly 30 to impart an optional rotational motion 54 to mandrel 40 and the substrate 50 formed along mandrel 40 to impart an increase in the circumferential strength of substrate 50 during the dip-coating process, as described in further detail below.

The assembly 30 may be isolated on a vibration-damping or vibrationally isolated table to ensure that the liquid surface held within container 44 remains completely undisturbed to facilitate the formation of a uniform thickness of polymer material along mandrel 40 and/or substrate 50 with each deposition The entire assembly 30 or just a portion of the assembly such as the mandrel 40 and polymer solution may be placed in an inert environment such as a nitrogen gas environment while maintaining a very low relative humidity (RH) level, e.g., less than 30% RH, and appropriate dipping temperature, e.g., at least 20° C. below the boiling point of the solvent within container 44 so as to ensure adequate bonding between layers of the dip-coated substrate. Multiple mandrels may also be mounted along bracket arm 38 or directly to column 34.

The mandrel 40 may be sized appropriately and define a cross-sectional geometry to impart a desired shape and size to the substrate 50. Mandrel 40 may be generally circular in cross section although geometries may be utilized as desired. In one example, mandrel 40 may define a circular geometry having a diameter ranging from 1 mm to 20 mm to form a polymeric substrate having a corresponding inner diameter. Moreover, mandrel 40 may be made generally from various materials which are suitable to withstand dip-coating processes, e.g., stainless steel, copper, aluminum, silver, brass, nickel, titanium, etc. The length of mandrel 40 that is dipped into the polymer solution may be optionally limited in length by, e.g., 50 cm, to ensure that an even coat of polymer is formed along the dipped length of mandrel 40 to limit the effects of gravity during the coating process. Mandrel 40 may also be made from a polymeric material which is lubricious, strong, has good dimensional stability, and is chemically resistant to the polymer solution utilized for dip-coating, e.g., fluoropolymers, polyacetal, polyester, polyimide, polyacrylates, etc.

Moreover, mandrel 40 may be made to have a smooth surface for the polymeric solution to form upon. In other variations, mandrel 40 may define a surface that is coated with a material such as polytetrafluroethylene to enhance removal of the polymeric substrate formed thereon. In yet other variations, mandrel 40 may be configured to define any number of patterns over its surface, e.g., either over its entire length or just a portion of its surface, that can be mold-transferred during the dip-coating process to the inner surface of the first layer of coating of the dip-coated substrate tube. The patterns may form raised or depressed sections to form various patterns such as checkered, cross-hatched, cratered, etc. that may enhance endothelialization with the surrounding tissue after the device is implanted within a patient, e.g., within three months or of implantation.

The direction that mandrel 40 is dipped within polymeric solution 46 may also be alternated or changed between layers of substrate 50. In forming substrates having a length ranging from, e.g., 1 cm to 40 cm or longer, substrate 50 may be removed from mandrel 40 and replaced onto mandrel 40 in an opposite direction before the dipping process is continued. Alternatively, mandrel 40 may be angled relative to bracket arm 38 and/or polymeric solution 46 during or prior to the dipping process.

This may also be accomplished in yet another variation by utilizing a dipping assembly as illustrated in FIGS. 2B and 2C to achieve a uniform wall thickness throughout the length of the formed substrate 50 per dip. For instance, after 1 to 3 coats are formed in a first dipping direction, additional layers formed upon the initial layers may be formed by dipping mandrel 40 in a second direction opposite to the first dipping direction, e.g., angling the mandrel 40 anywhere up to 180° from the first dipping direction. This may be accomplished in one example through the use of one or more pivoting linkages 56, 58 connecting mandrel 40 to bracket arm 38, as illustrated. The one or more linkages 56, 58 may maintain mandrel 40 in a first vertical position relative to solution 46 to coat the initial layers of substrate 50, as shown in FIG. 2B. Linkages 56, 58 may then be actuated to reconfigure mandrel 40 from its first vertical position to a second vertical position opposite to the first vertical position, as indicated by direction 59 in FIG. 2C. With repositioning of mandrel 40 complete, the dipping process may be resumed by dipping the entire linkage assembly along with mandrel 40 and substrate 50. In this manner, neither mandrel 40 nor substrate 50 needs to be removed and thus eliminates any risk of contamination. Linkages 56, 58 may comprise any number of mechanical or electromechanical pivoting and/or rotating mechanisms as known in the art.

Dipping mandrel 40 and substrate 50 in different directions may also enable the coated layers to have a uniform thickness throughout from its proximal end to its distal end to help compensate for the effects of gravity during the coating process. These values are intended to be illustrative and are not intended to be limiting in any manner. Any excess dip-coated layers on the linkages 56, 58 may simply be removed from mandrel 40 by breaking the layers. Alternating the dipping direction may also result in the polymers being oriented alternately which may reinforce the tensile strength in the axial direction of the dip coated tubular substrate 50.

With dip-coating assembly 30, one or more high molecular weight biocompatible and/or bioabsorbable polymers may be selected for forming upon mandrel 40. Examples of polymers which may be utilized to form the polymeric substrate may include, but is not limited to, polyethylene, polycarbonates, polyamides, polyesteramides, polyetheretherketone, polyacetals, polyketals, polyurethane, polyolefin, or polyethylene terephthalate and degradable polymers, for example, polylactide (PLA) including poly-L-lactide (PLLA), poly-glycolide (PGA), poly(lactide-co-glycolide) (PLGA) or polycaprolactone, caprolactones, polydioxanones, polyanhydrides, polyorthocarbonates, polyphosphazenes, chitin, chitosan, poly (amino acids), and polyorthoesters, and copolymers, terpolymers and combinations and mixtures thereof.

Other examples of suitable polymers may include synthetic polymers, for example, oligomers, homopolymers, and co-polymers, acrylics such as those polymerized from methyl cerylate, methyl methacrylate, acryli acid, methacrylic acid, acrylamide, hydroxyethy acrylate, hydroxyethyl methacrylate, glyceryl scrylate, glyceryl methacrylate, methacrylamide and ethacrylamide; vinyls such as styrene, vinyl chloride, binaly pyrrolidone, polyvinyl alcohol, and vinyls acetate; polymers formed of ethylene, propylene, and tetrfluoroethylene. Further examples may include nylons such as polycoprolactam, polylauryl lactam, polyjexamethylene adipamide, and polyexamethylene dodecanediamide, and also polyurethanes, polycarbonates, polyamides, polysulfones, poly(ethylene terephthalate), polyactic acid, polyglycolic acid, polydimethylsiloxanes, and polyetherketones.

Examples of biodegradable polymers which can be used for dip-coating process are polylactide (PLA), polyglycolide (PGA), poly(lactide-co-glycolide) (PLGA), poly(e-caprolactone), polydioxanone, polyanhydride, trimethylene carbonate, poly(β-hydroxybutyrate), poly(g-ethyl glutamate), poly(DTH iminocarbonate), poly(bisphenol A iminocarbonate), poly(ortho ester), polycyanoacrylate, and polyphosphazene, and copolymers, terpolymers and combinations and mixtures thereof. There are also a number of biodegradable polymers derived from natural sources such as modified polysaccharides (cellulose, chitin, chitosan, dextran) or modified proteins (fibrin, casein).

Other examples of suitable polymers may include synthetic polymers, for example, oligomers, homopolymers, and co-polymers, acrylics such as those polymerized from methyl cerylate, methyl methacrylate, acryli acid, methacrylic acid, acrylamide, hydroxyethy acrylate, hydroxyethyl methacrylate, glyceryl scrylate, glyceryl methacrylate, methacrylamide and ethacrylamide; vinyls such as styrene, vinyl chloride, binaly pyrrolidone, polyvinyl alcohol, and vinyls acetate; polymers formed of ethylene, propylene, and tetrfluoroethylene. Further examples may include nylons such as polycoprolactam, polylauryl lactam, polyjexamethylene adipamide, and polyexamethylene dodecanediamide, and also polyurethanes, polycarbonates, polyamides, polysulfones, poly(ethylene terephthalate), polyacetals, polyketals, polydimethylsiloxanes, and polyetherketones.

These examples of polymers which may be utilized for forming the substrate are not intended to be limiting or exhaustive but are intended to be illustrative of potential polymers which may be used. As the substrate may be formed to have one or more layers overlaid upon one another, the substrate may be formed to have a first layer of a first polymer, a second layer of a second polymer, and so on depending upon the desired structure and properties of the substrate. Thus, the various solutions and containers may be replaced beneath mandrel 40 between dip-coating operations in accordance with the desired layers to be formed upon the substrate such that the mandrel 40 may be dipped sequentially into the appropriate polymeric solution.

Depending upon the desired wall thickness of the formed substrate, the mandrel 40 may be dipped into the appropriate solution as determined by the number of times the mandrel 40 is immersed, the duration of time of each immersion within the solution, as well as the delay time between each immersion or the drying or curing time between dips. Additionally, parameters such as the dipping and/or withdrawal rate of the mandrel 40 from the polymeric solution may also be controlled to range from, e.g., 5 mm/min to 1000 min/min. Formation via the dip-coating process may result in a polymeric substrate having half the wall thickness while retaining an increased level of strength in the substrate as compared to an extruded polymeric structure. For example, to form a substrate having a wall thickness of, e.g., 200 μm, built up of multiple layers of polylactic acid, mandrel 40 may be dipped between, e.g., 2 to 20 times or more, into the polymeric solution with an immersion time ranging from, e.g., 15 seconds (or less) to 240 minutes (or more. Moreover, the substrate and mandrel 40 may be optionally dried or cured for a period of time ranging from, e.g., 15 seconds (or less) to 60 minutes (or more) between each immersion. These values are intended to be illustrative and are not intended to be limiting in any manner.

Aside from utilizing materials which are relatively high in molecular weight, another parameter which may be considered in further increasing the ductility of the material is its crystallinity, which refers to the degree of structural order in the polymer. Such polymers may contain a mixture of crystalline and amorphous regions where reducing the percentage of the crystalline regions in the polymer may further increase the ductility of the material. Polymeric materials not only having a relatively high molecular weight but also having a relatively low crystalline percentage may be utilized in the processes described herein to form a desirable tubular substrate.

The following Table 1 show examples of various polymeric materials e.g., PLLA IV 8.28 and PDLLA 96/4) to illustrate the molecular weights of the materials in comparison to their respective crystallinity percentage. The glass transition temperature, T_(g), as well as melting temperature, T_(m), are given as well. An example of PLLA IV 8.28 is shown illustrating the raw resin and tube form as having the same molecular weight, M_(w), of 1.70×10⁶ gram/mol. However, the crystallinity percentage of PLLA IV 8.28 Resin is 61.90% while the corresponding Tube form is 38.40%. Similarly for PDLLA 96/4, the resin form and tube form each have a molecular weight, M_(w), of 9.80×10⁵ gram/mol; however, the crystallinity percentages are 46.20% and 20.90%, respectively.

TABLE 1 Various polymeric materials and their respective crystallinity percentages. Crystallinity M_(w) Material T_(g) (° C.) T_(m) (° C.) (%) (gram/mol) PLLA IV8.28 72.5 186.4 61.90% 1.70 × 10⁶ Resin PLLA IV8.28 73.3 176.3 38.40% 1.70 × 10⁶ Tubes PDLLA 96/4 61.8 155.9 46.20% 9.80 × 10⁵ Resin PDLLA 96/4 60.3 146.9 20.90% 9.80 × 10⁵ Tubes

As the resin is dip coated to for the tubular substrate through the methods described herein, the drying procedures and processing helps to preserve the relatively high molecular weight of the polymer from the starting material and throughout processing to substrate and stent formation. Moreover, the drying processes in particular may facilitate the formation of desirable crystallinity percentages, as described above.

Aside from the crystallinity of the materials, the immersion times as well as drying times may be uniform between each immersion or they may be varied as determined by the desired properties of the resulting substrate. Moreover, the substrate may be placed in an oven or dried at ambient temperature between each immersion or after the feral immersion to attain a predetermined level of crystals, e.g., 60%, and a level of amorphous polymeric structure, e.g., 40%. Each of the layers overlaid upon one another during the dip-coating process are tightly adhered to one another and the mechanical properties of each polymer are retained in their respective layer with no limitation on the molecular weight of the polymers utilized.

Any number of PLLA polymers having a molecular weight within a range, for instance, between 4.3 and 8.4 may be utilized. Alternatively, a polymeric substrate characterized by a length, an inner diameter, an outer diameter and a thickness, comprising a bioresorbable polymer may be characterized by a molecular weight from, e.g., 259,000 g/mol to 2,120,000 g/mol with a crystallinity from, e.g., 20% to 40%, or more particularly from, e.g., 27% to 35%.

Varying the drying conditions of the materials may also be controlled to effect desirable material parameters. The polymers may be dried at or above the glass transition temperature (e.g., 10° to 20° C. above the glass transition temperature, T_(g)) of the respective polymer to effectively remove any residual solvents from the polymers to attain residual levels of less than 100 ppm, e.g., between 20 to 100 ppm. Positioning of the polymer substrate when drying is another factor which may be controlled as affecting parameters, such as geometry, of the tube. For instance, the polymer substrate may be maintained in a drying position such that the substrate tube is held in a perpendicular position relative to the ground such that the concentricity of the tubes is maintained. The substrate tube may be dried in an oven at or above the glass transition temperature, as mentioned, for a period of time ranging anywhere from, e.g., 10 days to 30 days or more. However, prolonged drying for a period of time, e.g., greater than 40 days, may result in thermal degradation of the polymer material.

Additionally and/or optionally, a shape memory effect may be induced in the polymer during drying of the substrate. For instance, a shape memory effect may be induced in the polymeric tubing to set the tubular shape at the diameter that was formed during the dip-coating process. An example of this is to form a polymeric tube by a dip-coating process described herein at an outer diameter of 5 mm and subjecting the substrate to temperatures above its glass transition temperature, T_(g). At its elevated temperature, the substrate may be elongated, e.g., from a length of 5 cm to 7 cm, while its outer diameter of 5 min is reduced to 3 mm. Of course, these examples are merely illustrative and the initial diameter may generally range anywhere from, e.g., 3 mm to 9 mm, and the reduced diameter may generally range anywhere from, e.g., 1.5 mm to 5 mm, provided the reduced diameter is less than the initial diameter.

Once lengthened and reduced in diameter, the substrate may be quenched or cooled in temperature to a sub-T_(g) level, e.g., about 20° C. below its T_(g), to allow for the polymeric substrate to transition back to its glass state. This effectively imparts a shape memory effect of self-expansion to the original diameter of the substrate. When such a tube (or stent formed from the tubular substrate) is compressed or expanded to a smaller or larger diameter and later exposed to an, elevated temperature, over time the tube (or stent) may revert to its original 5 mm diameter. This post processing may also be useful for enabling self-expansion of the substrate after a process like laser cutting (e.g., when forming stents or other devices for implantation within the patient) where the substrate tube is typically heated to its glass transition temperature, T_(g).

An example of a substrate having multiple layers is illustrated in FIGS. 3A and 3B which show partial cross-sectional side views of an example of a portion of a multi-layer polymeric substrate formed along mandrel 40 and the resulting substrate. Substrate 50 may be formed along mandrel 40 to have a first layer 60 formed of a first polymer, e.g., poly-(l-lactide). After the formation of first layer 60, an optional second layer 62 of polymer, e.g., poly(L-lactide-co-glycolide), may be formed upon first layer 60. Yet another optional third layer 64 of polymer, e.g., poly(d,l-lactide-co-glycolide), may be formed upon second layer 62 to form a resulting substrate defining a lumen 66 therethrough which may be further processed to form any number of devices, such as a stent. One or more of the layers may be formed to degrade at a specified rate or to elute any number of drugs or agents.

An example of this is illustrated in the cross-sectional end view of FIG. 3C. which shows an exemplary substrate having three layers 60, 62, 64 formed upon one another, as above. In this example, first layer 60 may have a molecular weight of M_(n1), second layer 62 may have a molecular weight of M_(n2), and third layer 64 may have a molecular weight of M_(n3). A stent fabricated from the tube may be formed such that the relative molecular weights are such where M_(n1)>M_(n2)>M_(n3) to achieve a preferential layer-by-layer degradation through the thickness of the tube beginning with the inner first layer 60 and eventually degrading to the middle second layer 62 and finally to the outer third layer 64 when deployed within the patient body. Alternatively, the stent may be fabricated where the relative molecular weights are such where M_(n1)<M_(n2)<M_(n3) to achieve a layer-by-layer degradation beginning with the outer third layer 64 and degrading towards the inner first layer 60. This example is intended to be illustrative and fewer than or more than three layers may be utilized in other examples. Additionally, the molecular weights of each respective layer may be altered in other examples to vary the degradation rates along different layers, if so desired.

Moreover, any one or more of the layers may be formed to impart specified mechanical properties to the substrate 50 such that the composite mechanical properties of the resulting substrate 50 may specifically tuned or designed. Additionally, although three layers are illustrated in this example, any number of layers may be utilized depending upon the desired mechanical properties of the substrate 50.

Moreover, as multiple layers may be overlaid one another in forming the polymeric substrate, specified layers may be designated for a particular function in the substrate. For example, in substrates which are used to manufacture polymeric stents, one or more layers may be designed as load-bearing layers to provide structural integrity to the stent while certain other layers may be allocated for drug-loading or eluting. Those layers which are designated for structural support may be formed from high-molecular weight polymers, e.g., PLLA or any other suitable polymer described herein, to provide a high degree of strength by omitting any drugs as certain pharmaceutical agents may adversely affect the mechanical properties of polymers. Those layers which are designated for drug-loading may be placed within, upon, or between the structural layers.

Additionally, multiple layers of different drugs may be loaded within the various layers. The manner and rate of drug release from multiple layers may depend in part upon the degradation rates of the substrate materials. For instance, polymers which degrade relatively quickly may release their drugs layer-by-layer as each successive layer degrades to expose the next underlying layer. In other variations, drug release may typically occur from a multilayer matrix via a combination of diffusion and degradation. In one example, a first layer may elute a first drug for, e.g., the first 30 to 40 days after implantation. Once the first layer has been exhausted or degraded, a second underlying layer having a second drug may release this drug for the next 30 to 40 days, and so on if so desired. In the example of FIG. 3B, for a stent (or other implantable device) manufactured from substrate 50, layer 64 may contain the first drug for release while layer 62 may contain the second drug for release after exhaustion or degradation of layer 64. The underlying layer 60 may omit any pharmaceutical agents to provide uncompromised structural support to the entire structure.

In other examples, rather than having each successive layer elute its respective drug, each layer 62, 64 (optionally layer 60 as well), may elute its respective drug simultaneously or at differing rates via a combination of diffusion and degradation. Although three layers are illustrated in this example, any number of layers may be utilized with any practicable combination of drugs for delivery. Moreover, the release kinetics of each drug from each layer may be altered in a variety of ways by changing the formulation of the drug-containing layer.

Examples of drugs or agents which may be loaded within certain layers of substrate 50 may include one or more antipoliferative, antineoplastic, antigenic, anti-inflammatory, and/or antirestenotic agents. The therapeutic agents may also include antilipid, antimitotics, metalloproteinase inhabitors, anti-sclerosing agents. Therapeutic agents may also include peptides, enzymes, radio isotopes or agents for a variety of treatment options. This list of drugs or agents is presented to be illustrative and is not intended to be limiting.

Similarly certain other layers may be loaded with radio-opaque substances such as platinum, gold, etc. to enable visibility of the stent under imaging modalities such as fluoroscopic imaging. Radio-opaque substances like tungsten, platinum, gold, etc. can be mixed with the polymeric solution and dip-coated upon the substrate such that the radio-opaque substances form a thin sub-micron thick layer upon the substrate. The radio-opaque substances may thus become embedded within layers that degrade in the final stages of degradation or within the structural layers to facilitate stent visibility under an imaging modality, such as fluoroscopy, throughout the life of the implanted device before fully degrading or losing its mechanical strength. Radio-opaque marker layers can also be dip-coated at one or both ends of substrate 50, e.g., up to 0.5 mm from each respective end. Additionally, the radio-opaque substances can also be spray-coated or cast along a portion of the substrate 50 between its proximal and distal ends in a radial direction by rotating mandrel 40 when any form of radio-opaque substance is to be formed along any section of length of substrate 50. Rings of polymers having radio-opaque markers can also be formed as part of the structure of the substrate 50.

In an experimental example of the ductility and retention of mechanical properties, PLLA with Iv 8.4 (high molecular weight) was obtained and tubular substrates were manufactured utilizing the dip-coating process described herein. The samples were formed to have a diameter of 5 mm with a wall thickness of 200 μm and were comprised of 6 layers of PLLA 8.4. The mandrel was immersed 6 times into the polymeric solution and the substrates were dried or cured in an oven to obtain a 60% crystalline structure. At least two samples of tubular substrates were subjected to tensile testing and stress-strain plot 70 was generated from the stress-strain testing, as shown in FIG. 4A.

As shown in plot 70, a first sample of PLLA 8.4 generated a stress-strain curve 72 having a region of plastic failure 76 where the strain percentage increased at a relatively constant stress value prior to failure indicating a good degree of sample ductility. A second sample of PLLA 8.4 also generated a stress-strain curve 74 having a relatively greater region of plastic failure 78 also indicating a good degree of sample ductility.

Polymeric stents and other implantable devices made from such substrates may accordingly retain the material properties from the dip-coated polymer materials. The resulting stents, for instance, may exhibit mechanical properties which have a relatively high percentage ductility in radial, torsional, and or axial directions. An example of this is a resulting stent having an ability to undergo a diameter reduction of anywhere between 5% to 70% when placed under an external load without any resulting plastic deformation. Such a stent may also exhibit high radial strength with, e.g., a 20% radial deformation when placed under a 0.1 N to 20 N load. Such a stent may also be configured to self-expand when exposed to normal body temperatures.

The stent may also exhibit other characteristic mechanical properties which are consistent with a substrate formed as described herein, for instance, high ductility and high strength polymeric substrates. Such substrates (and processed stents) may exhibit additional characteristics such as a percent reduction in diameter of between 5% to 70% without fracture formation when placed under a compressive load as well as a percent reduction in axial length of between 10% to 30% without fracture formation when placed under an axial load. Because of the relatively high ductility, the substrate or stent may also be adapted to curve up to 180° about a 1 cm curvature radius without fracture formation or failure. Additionally, when deployed within a vessel, a stent may also be expanded, e.g., by an inflatable intravascular balloon, by up to 5% to 70% to regain diameter without fracture formation or failure.

These values are intended to illustrate examples of how a polymeric tubing substrate and a resulting stent may be configured to yield a device with certain mechanical properties. Moreover, depending upon the desired results, certain tubes and stents may be tailored for specific requirements of various anatomical locations within a patient body by altering the polymer and/or copolymer blends to adjust various properties such as strength, ductility, degradation rates, etc.

FIG. 4B illustrates a plot 71 of additional results from stress-strain testing with additional polymers. A sample of PLLA 8.28 was formed utilizing the methods described herein and tested to generate stress-strain curve 73 having a point of failure 73′. Additional samples of PLLA 8.28 each with an additional layer of BaSO₄ incorporated into the tubular substrate were also formed and tested. A first sample of PLLA 8.28 with a layer of BaSO₄ generated stress-strain curve 77 having a point of failure 77′. A second sample of PLLA 8.28 also with a layer of BaSO₄ generated stress-strain curve 79 having a point of failure 79′, which showed a greater tensile strain than the first sample with a slightly higher tensile stress level. A third sample of PLLA 8.28 with a layer of BaSO₄ generated stress-strain curve 81 having a point of failure 81′, which was again greater than the tensile strain of the second sample, yet not significantly greater than the tensile stress level. The inclusion of BaSO₄ may accordingly improve the elastic modulus values of the polymeric substrates. The samples of PLLA 8.28 generally resulted in a load of between 100 N to 300 N at failure of the materials, which yielded elastic modulus values of between 1000 to 3000 MPa with a percent elongation of between 10% to 300% at failure.

A sample of 96/4 PDLLA was also formed and tested to generate stress-strain curve 75 having a point of failure 75′ which exhibited a relatively lower percent elongation characteristic of brittle fracture. The resulting load at failure was between 100 N to 300 N with an elastic modulus of between 1000 to 3000 MPa, which was similar to the PLLA 8.28 samples. However, the percent elongation was between 10% to 40% at failure.

FIG. 4C illustrates an example of a detailed end view of a PLLA 8.28 substrate 83 formed with multiple dip-coated layers via a process described herein as viewed under a scanning electron microscope. This variation has a BaSO₄ layer 85 incorporated into the substrate. As described above, one or more layers of BaSO₄ may be optionally incorporated into substrate 83 to alter the elastic modulus of the formed substrate. Additionally, the individual layers overlaid atop one another are fused to form a single cohesive layer rather than multiple separate layers as a result of the drying processes during the dipping process described herein. This results in a unitary structure which further prevents or inhibits any delamination from occurring between the individual layers.

FIGS. 5A and 5B illustrate perspective views of one of the samples which was subjected to stress-strain testing on tensile testing system 80. The polymeric substrate specimen 86 was formed upon a mandrel, as described above, into a tubular configuration anti secured to testing platform 82, 84. With testing platform 82, 84 applying tensile loading, substrate specimen 86 was pulled until failure. The relatively high percentage of elongation is illustrated by the stretched region of elongation 88 indicating a relatively high degree of plastic deformation when compared to an extruded polymeric substrate. Because a polymeric substrate formed via dip-coating as described above may be reduced in diameter via plastic deformation without failure, several different stent diameters can be manufactured from a single diameter substrate tube.

Dip-coating can be used to impart an orientation between layers (e.g., linear orientation by dipping; radial orientation by spinning the mandrel; etc.) to further enhance the mechanical properties of the formed substrate. As radial strength is a desirable attribute of stent design, post-processing of the formed substrate may be accomplished to impart such attributes. Typically, polymeric stents suffer from having relatively thick walls to compensate for the lack of radial strength, and this in turn reduces flexibility, impedes navigation, and reduces arterial luminal area immediately post implantation. Post-processing may also help to prevent material creep and recoil (creep is a time-dependent permanent deformation that occurs to a specimen under stress, typically under elevated temperatures) which are problems typically associated with polymeric stents.

In further increasing the radial or circumferential strength of the polymeric substrate, a number of additional processes may be applied to the substrate after the dip-coating procedure is completed (or close to being completed). A polymer that is amorphous or that is partially amorphous will generally undergo a transition from a pliable, elastic state (at higher temperatures) to a brittle glass-like state (at lower temperature) as it transitions through a particular temperature, referred as the glass transition temperature (T_(g)). The glass transition temperature for a given polymer will vary, depending on the size and flexibility of side chains, as well as the flexibility of the backbone linkages and the size of functional groups incorporated into the polymer backbone. Below T_(g), the polymer will maintain some flexibility, and may be deformed to a new shape. However, the further the temperature below T_(g) the polymer is when being deformed, the greater the force needed to shape it.

Moreover, when a polymer is in glass transition temperature its molecular structure can be manipulated to form an orientation in a desired direction. Induced alignment of polymeric chains or orientation improves mechanical properties and behavior of the material. Molecular orientation is typically imparted by application of force while the polymer is in a pliable, elastic state. After sufficient orientation is induced, temperature of the polymer is reduced to prevent reversal and dissipation of the orientation.

In one example, the polymeric substrate may be heated to increase its temperature along its entire length or along a selected portion of the substrate to a temperature that is at or above the T_(g) of the polymer. For instance, for a substrate fabricated from PLLA, the substrate may be heated to a temperature between 60° C. to 70° C. Once the substrate has reached a sufficient temperature such that enough of its molecules have been mobilized, a force may be applied from within the substrate or along a portion of the substrate to increase its diameter from a first diameter D₁ to a second increased diameter D₂ for a period of time necessary to set the increased diameter. During this setting period, the application of force induces a molecular orientation in a circumferential direction to align the molecular orientation of polymer chains to enhance its mechanical properties. The re-formed substrate may then be cooled to a lower temperature typically below T_(g), for example, by passing the tube through a cold environment, typically dry air or an inert gas to maintain the shape at diameter D₂ and prevent dissipation of molecular orientation.

The force applied to the substrate may be generated by a number of different methods. One method is by utilizing an expandable pressure vessel placed within the substrate. Another method is by utilizing a braid structure, such as a braid made from a super-elastic or shape memory alloy like NiTi alloy, to increase in size and to apply the desirable degree of force against the interior surface of the substrate.

Yet another method may apply the expansion force by application of a pressurized inert gas such as nitrogen within the substrate lumen, as shown in FIG. 6, to impart a circumferential orientation in the substrate. A completed substrate, e.g., cast cylinder 94, may be placed inside a molding tube 90 which has an inner diameter that is larger than the cast cylinder 94. Molding tube 90 may be fabricated from glass, highly-polished metal, or polymer. Moreover, molding tube 90 may be fabricated with tight tolerances to allow for precision sizing of cast cylinder 94.

A distal end or distal portion of cast cylinder 94 may be clamped 96 or otherwise closed and a pressure source may be coupled to a proximal end 98 of cast cylinder 94. The entire assembly may be positioned over a nozzle 102 which applies heat 104 to either the length of cast cylinder 94 or to a portion of cast cylinder 94. The pressurized inert gas 100, e.g., pressured to 10 to 400 psi, may be introduced within cast cylinder 94 to increase its diameter, e.g., 2 mm, to that of the inner diameter, e.g., 4 mm, of molding tube 90. The increase in diameter of cast cylinder 94 may thus realign the molecular orientation of cast cylinder 94 to increase its radial strength and to impart a circumferential orientation in the cast cylinder 94. Portion 92 illustrates radial expansion of the cast cylinder 94 against the inner surface of the molding tube 90 in an exaggerated manner to illustrate the radial expansion and impartation of circumferential strength. After the diameter has been increased, cast cylinder 94 may be cooled, as described above.

Once the substrate has been formed and reduced in diameter to its smaller second diameter, the stent may be processed, as described above. Alternatively, the stent may be processed from the substrate after initial formation. The stent itself may then be reduced in diameter to its second reduced diameter.

In either case, once the stent has been formed into its second reduced diameter, the stent may be delivered to a targeted location within a vessel of a patient. Delivery may be effected intravascularly utilizing known techniques with the stent in its second reduced delivery diameter positioned upon, e.g., an inflation balloon, for intravascular delivery. Once the inflation catheter and stent has been positioned adjacent to the targeted region of vessel, the stent may be initially expanded into contact against the interior surface of the vessel.

With the stent expanded into contact against the vessel wall at a third diameter which is larger than the second delivery diameter, the inflation balloon may be removed from the stent. Over a predetermined period of time and given the structural characteristics of the stent, the stent may then also self-expand further into contact against the vessel wall for secure placement and positioning.

Because thermoplastic polymers such as PLLA typically soften when heated, the cast cylinder 94 or a portion of the cast cylinder 94 may be heated in an inert environment, e.g., a nitrogen gas environment, to minimize its degradation.

Another method for post-processing a cast cylinder 110 may be seen in the example of FIG. 7 for inducing a circumferential orientation in the formed substrate. As illustrated, mandrel 112 having the cast cylinder 110 may be re-oriented into a horizontal position immediately post dip-coating before the polymer is cured. Mandrel 112 may be rotated, as indicated by rotational movement 116, at a predetermined speed, e.g., 1 to 300 rpm, while the cylinder 110 is heated via nozzle 102. Mandrel 112 may also be optionally rotated via motor 48 of assembly 30 to impart the rotational motion 54, as shown above in FIG. 2. Mandrel 112 may also be moved in a linear direction 114 to heat the length or a portion of the length of the cylinder 110. As above, this post-processing may be completed in an inert environment.

Once the processing has been completed on the polymeric substrate, the substrate may be further formed or machined to create a variety of device. One example is shown in the perspective view of FIG. 8, which illustrates rolled stent 120. Stent 120 may be created from the cast cylinder by cutting along a length of the cylinder to create an overlapping portion 122. The stent 120 may then be rolled into a small configuration for deployment and then expanded within the patient vasculature. Another example is illustrated in the side view of stent 124, which may be formed by machining a number of removed portions 126 to create a lattice or scaffold structure which facilitates the compression and expansion of stent 124 for delivery and deployment.

FIGS. 10A to 10F illustrate side views of another example of how a stent 130 formed from a polymeric substrate may be delivered and deployed for secure expansion within a vessel. FIG. 10A shows a side view of an exemplary stent 130 which has been processed or cut from a polymeric substrate formed with an initial diameter D1. As described above, the substrate may be heat treated at, near, or above the glass transition temperature T_(g) of the substrate to set this initial diameter D1 and the substrate may then be processed to produce the stent 130 such that the stent 130 has a corresponding diameter D1. Stent 130 may then be reduced in diameter to a second delivery diameter D2 which is less than the initial diameter D1 such that the stent 130 may be positioned upon, e.g., an inflation balloon 134 of a delivery catheter 132, as shown in FIG. 10B. The stent 130 at its reduced diameter D2 may be self-constrained such that the stent 130 remains in its reduced diameter D2 without the need for an outer sheath, although a sheath may be optionally utilized. Additionally, because of the processing and the resultant material characteristics of the stent material, as described above, the stent 130 may be reduced from initial diameter D1 to delivery diameter D2 without cracking or material failure.

With stent 130 positioned upon delivery catheter 132, it may be advanced intravascularly within a vessel 136 until the delivery site is reached, as shown in FIG. 10C. Inflation balloon 134 may be inflated to expand a diameter of stent 130 into contact against the vessel interior, e.g., to an intermediate diameter D3, which is less than the stent's initial diameter D1 yet larger than the delivery diameter D2. Stent 130 may be expanded to this intermediate diameter D3 without any cracking or failure because of the inherent material characteristics described above. Moreover, expansion to intermediate diameter D3 may allow for the stent 130 to securely contact the vessel wall while allowing for the withdrawal of the delivery catheter 132, as shown in FIG. 10E.

Once the stent 130 has been expanded to some intermediate diameter D3 and secured against the vessel wall, stent 130 may be allowed to then self-expand further over a period of time into further contact with the vessel wall such that stent 130 conforms securely to the tissue. This self-expansion feature ultimately allows for the stent 130 to expand back to its initial diameter D1 which had been heat set, as shown in FIG. 10F, or until stent 130 has fully self-expanded within the confines of the vessel diameter.

Side Branch Access

A blood vessel often has numerous side-branches that vascularize tissues that are relatively far from the main vessel. One example is shown in FIG. 11A which illustrates a main vessel MV with a side branch SB extending from the main vessel MV. A vessel such as the main vessel MV may have multiple side branches but a single side branch SB is shown merely for illustrative purposes. When the vessels develop a disease, e.g., arteriosclerosis that obstructs the flow within the main vessel MV, side branch SB, or both, the obstruction may occur at the junction of the main vessel MV and one of its side branches SB, FIG. 11B illustrates an example where multiple lesions LS1, LS2, LS3 are formed at the junction between the main vessel MV and side branch SB where lesions LS1, LS2 are formed between the main vessel MV and side branch SB and where lesion LS3 is formed within the main vessel MV in proximity to where side branch SB extends from the main vessel MV.

If flow patency in both the main vessel MV and the side branch SB is desired, one can deploy a stent 140 in the main vessel MV at the junction where the side branch SB extends and then treat the side branch SB with balloon angioplasty or by stenting. However, the stent 140 that has been placed in the main vessel MV may obstruct part of the opening to the side branch SB and cause flow reduction or other negative effects, as shown in FIG. 12. As further illustrated, a detail top view is also shown in FIG. 12 illustrating a view into and through the side branch SB to the junction where the expanded stent 140 is positioned. The circumferential rings 142 and longitudinal struts 144 which join adjacent rings 142 to one another may be seen expanded against the vessel walls within the main vessel MV; however, these scaffolding members are also seen to partially obstruct the opening to the side branch SB.

In order to reduce the side branch flow obstruction, a practitioner can expand the junction between the main vessel MV and the side branch SB, e.g., with an angioplasty balloon or with a stent. Doing so may require a balloon catheter or a stent to be tracked within the main vessel MV, into the expanded stent 140, and then through an open cell defined along the main vessel stent 140 adjacent to the opening of the side branch SB, as shown by pathway 150 in the schematic side view of FIG. 13A. Once the catheter 152 has been advanced along pathway 150, an inflatable balloon 154 (or other expansion mechanism) located along the catheter 152, may be positioned within an expanded open cell 146 (as shown in the side view of FIG. 13B) which is located at or in proximity to the opening of the side branch SB where a periphery of the open cell 146 is defined by adjacent circumferential rings 142 and longitudinal struts 144 framing the open cell 146. The inflatable balloon 154 may then be expanded to enlarge the open cell 146 to a further enlarged configuration without disrupting or reconfiguring the remainder of the stent 140 to provide a more open flow path through the opening to the side branch SB.

Any of the polymeric scaffold or stent embodiments described herein are particularly suitable for expanding one or more open cells of the stent because the material characteristics of the resulting stent enable the further enlargement of the open cells without fracturing or cracking the stent struts. Hence, the polymeric substrate and stent assemblies as described in the following are particularly well-suited for the methods and apparatus described below: U.S. patent application Ser. No. 10/867,617 filed Jun. 15, 2004 (U.S. Pub. 2005/0021131); Ser. No. 13/476,853 filed May 21, 2012 (U.S. Pub. 2012/0232643); Ser. No. 13/476,858 filed May 21, 2012 (U.S. Pub. 2012/0232644); Ser. No. 12/541,095 filed Aug. 13, 2009 (U.S. Pub. 2010/0042202); U.S. Pat. Nos. 8,574,493; 8,206,635; 8,206,636; and 8,309,023. Each of these references is incorporated herein by reference in its entirety for any purpose herein.

FIGS. 14A and 14B show detail top views through the side branch SB and into the main vessel MV with the stent 140 in its deployed and expanded configuration against the interior vessel walls. The open cell 146 located at the opening of the side branch SB may be seen highlighted for illustrative purposes in FIG. 14A in a first configuration when deployed and expanded. After a balloon catheter has been positioned within the open cell and expanded, the resulting enlarged open cell 146′ (also highlighted for illustrative purposes) may be seen in FIG. 14B having a second configuration which is enlarged compared to the first configuration shown in FIG. 14A.

FIGS. 15A and 15B show top views of the stent 140 outside of the main vessel MV in its expanded first configuration with open cell 146 (shown in FIG. 15A) and its second configuration with open cell 146′ (shown in FIG. 15B) in its further enlarged configuration. The size increase of the open cell 146′ facilitates not only access to the side branch SB from the main vessel MV but also facilitates blood flow due to the increased flow volume.

Typically, the size of the inflation balloon positioned within the open cell 146 may range for expansion of the stent struts to facilitate bifurcation access. One example may utilize an expansion of the inflation balloon to a diameter of, e.g., 2.0 mm to 4.5 mm. The expanded open cell 146′ may result in an actual opening having a similar opening diameter range. The inflatable balloon 154 may accordingly be inflated at a pressure of, e.g., 5 atm to 30 atm. The corresponding rings 142 and longitudinal struts 144 may be elongated without cracking, fracturing, or failing anywhere from, e.g., 2% to 120%, due to the combination of intrinsic properties not only of the polymer (e.g., yield, percent elongation at failure, etc.) but also due to the geometric dimensions of the stent 140 and its individual struts.

In order for side branch treatment to be feasible with a polymeric stent, the material and design desirably allows expansion of an open cell 146 to a desired diameter without causing cracks or fractures as well as maintaining a reasonable fatigue life. Moreover, because of the intrinsic material characteristics of the stent 140, the struts may be dilated and elongated to provide for side branch SB access without causing distortion, fracture, or separation of the surrounding stent structure. The energy generated by expansion of the balloon 154 is observed by the work involved in the strut's elongation which concentrates the energy in that specific zone hence virtually eliminating transmission of force to the rest of the stent 140.

Since expansion of the open cell 146 and side branch SB occurs in a circumferential manner due to the inflation of the balloon 154, the material of the stent allows for strain to occur isotropically. Particular PLLA tubes as shown and described in further detail in U.S. Pat. Nos. 8,206,635; 8,206,636; and 8,309,023 (each of which is incorporated herein by reference in its entirety and for any purpose herein) have homogeneous and isotropic properties throughout its structure which enhances its ability to accommodate side branch expansion.

Such particular PLLA tubes are constructed to have high molecular weight PLLA molecules (weight range). Such high molecular weight PLLA allows for much better elongation before break than tubes with lower molecular weight PLLA (80% elongation before break or better). Such material is critical to allowing side branch expansion.

Moreover, such particular stent design takes advantage of specified high molecular weight isotropic PLLA material property to distribute the stress and strain in order to allow side branch expansion without cracks or fractures while maintaining reasonable fatigue life. Dimensions, angles, and arrangement of the stent design elements minimize stress and strain experienced by the stent during normal use as well as side branch expansion. Open cell areas which are sized to allow balloons and stents to pass through may have stent ring structure angle designs limited to, e.g., 130 degrees, to allow further expansion while limiting strain. Moreover, design limit strain may he limited to, e.g., 70%, to prevent crack and fracture fomation within reasonable fatigue life.

As shown in FIG. 16, in order to make the stent 140 even more accommodating to side branch treatment, the stent struts 160 can incorporate strain relief features 162 that will deform to distribute strain. Such strain relief features 162 may include, for instance, struts which are curved or arcuate even when the stent 140 is initially expanded into its deployed configuration against the walls of the main vessel MV. These strain relief features 162 may enable the struts 160 to further elongate when reconfiguring the open cell 146 into its enlarged second configuration. The degree to which the struts 160 are curved or arcuate may vary, e.g., depending upon the degree of strain relief desired as well as the size of the enlarged second configuration.

Additionally, the stent design can incorporate specific openings that accommodate balloon/stent for side branch treatment. Such designs include, e.g., holes, open patterns, flaps, windows, slots, cell structures, and combinations thereof, etc., that allow for a sufficiently large enough opening for balloons/stents to pass through during side branch expansion while maintaining radial force and fatigue life.

Modification of the above-described methods and devices for carrying out the invention, and variations of aspects of the invention that are obvious to those of skill in the arts are intended to be within the scope of this disclosure. Moreover, various combinations of aspects between examples are also contemplated and are considered to be within the scope of this disclosure as well. 

1. (canceled)
 2. An expandable stent, comprising: an implantable stent scaffold having a lumen defined therethrough; wherein the implantable stent scaffold comprises a delivery configuration and a deployed configuration; wherein the implantable stein scaffold is expandable from the delivery configuration into the deployed configuration; wherein the implantable stent scaffold comprises at least one open cell defined along a wall of the implantable stein scaffold; wherein the at least one open cell is expandable from a first cell configuration into a second cell configuration by an expansion device introduced therein; and wherein the implantable stent scaffold is comprised of a bioresorbable polymer characterized by a molecular weight from about 259,000 g/mol to 2,120,000 g/mol and a crystallinity from about 20% to 40%.
 3. The stent of claim 1, further comprising one or more struts, wherein the one or more struts is capable of being elongated from about 2% to 120% without cracking, fracturing, or failing during expansion of the open cell.
 4. The stent of claim 3, wherein the one or more struts each define a strain relief area which is configured to stretch during expansion of the open cell.
 5. The stent of claim 1, wherein the open cell is configured to be expanded into the second cell configuration having a shape selected from the group consisting of a hole, a flap, a window, a slot, and combinations thereof.
 6. The stent of claim 5, wherein the open cell is configured to be expanded into a hole having a diameter between about 2.0 mm to 4.5 mm.
 7. The stern of claim 1 wherein the bioresorbable polymer is further characterized by a crystallinity from about 27% to 35%.
 8. The stent of claim 1 wherein the bioresorbable polymer is further characterized by crystalline regions and amorphous regions.
 9. The stern of claim 8, wherein the crystalline regions are isotropic.
 10. The stent of claim 8, wherein the crystalline regions are longitudinally oriented.
 11. The stent of claim 8, wherein the crystalline regions are circumferentially oriented.
 12. The stent of claim 1, wherein the physical properties of the bioresorbable polymer are isotropic.
 13. The stent of claim 1, wherein the bioresorbable polymer is further characterized by a solvent content of less than about 100 ppm.
 14. The stent of claim 1, wherein the bioresorbable polymer is further characterized by an intrinsic viscosity from about 4.3 dL/g to 8.4 dL/g
 15. The stent of claim 1, wherein the bioresorbable polymer is further characterized by an elastic modulus from about 1000 MPa to 3000 MPa.
 16. The stent of claim 1, wherein an applied load at failure of the implantable stent scaffold is from about 100 N to 300 N.
 17. The stent of claim 1, wherein the bioresorbable polymer is configured to curve up to 180° about a 1 cm curvature radius without fracture formation or failure.
 18. The stent of claim 1, wherein the implantable stent scaffold is characterized. by a radial strength of at least about 10 N per 1 cm length at about 20% compression
 19. The stent of claim 1, wherein the implantable stent scaffold is characterized by a radial strength of at least about 0.1 N to 5 N per 1 cm at 20% compression.
 20. The stent of claim 1, wherein the implantable stent scaffold is configured to withstand a strain of at least 150% without failure.
 21. The stent of claim 1, wherein the implantable stent scaffold is configured to self-expand from the delivery configuration into the deployed configuration. 